Silicon-germanium hydrides and methods for making and using same

ABSTRACT

The present invention provides novel silicon-germanium hydride compounds, methods for their synthesis, methods for their deposition, and semiconductor structures made using the novel compounds.

CROSS-REFERENCE TO RELATED APPLICATIONS

This application is a Continuation of U.S. patent application Ser. No. 12/093,256 filed Aug. 14, 2008, now U.S. Pat. No. 8,133,802, which is a U.S. National Phase of International Application No. PCT/US2006/045156, filed Nov. 21, 2006, which claims priority from U.S. Provisional Application No. 60/764,063 filed Feb. 1, 2006, which claims priority from U.S. Provisional Application No. 60/739,528 filed Nov. 23, 2005, which are incorporated herein by reference in their entirety.

STATEMENT OF GOVERNMENT INTEREST

This work was supported by National Science Foundation grant DMR-0221993 thus the U.S. government may have certain rights in the invention.

FIELD OF THE INVENTION

The present application relates generally to the fields of chemistry, optoelectronics, silicon-germanium alloys, semiconductor structures, and related methods and devices.

BACKGROUND

Heteroepitaxial Ge_(1-x)Si_(x) layers on Si(100) with high Ge contents are of interest due to many applications in key technologies such as solar cells, MEMS, quantum cascade lasers and Si-based photonics^(1,2) including high speed modulators and photodetectors.³ However, these materials are much less developed in spite of this high impact potential in IR optical devices. In addition, they serve as virtual substrates for growth of high mobility, strained Si and Ge device channels, and are also considered as a potential pathway to monolithic integration of III-V based devices with Si technologies.^(4,5) The best current route to these materials is complicated and fraught with difficulties, requiring both high temperature growth of thick (>10 μm) compositionally graded films and a chemical-mechanical planarization step to relieve the misfit strain between the Ge_(1-x)Si_(x) epilayer and Si substrate and produce a flat surface, respectively.⁶

To circumvent these difficulties we have recently developed new chemical vapor deposition (CVD) heteroepitaxy to produce device quality strain-relieved Ge-rich films on Si without the need for graded compositions.^(7,8) Our strategy involves depositions of single source hydride precursors with direct Si—Ge bonds such as the (H₃Ge)_(x)SiH_(4-x) (x=1-4) family of compounds. These are routinely synthesized with semiconductor grade purity via straightforward methodologies utilizing commercially available starting materials.⁷ Their physical and chemical properties such as high volatility and facile reactivity make them particularly useful as reagents in low temperature film growth by CVD and gas source molecular beam epitaxy (GSMBE). Our initial growth experiments have yielded single crystal films with compositions Si_(0.50)Ge_(0.50), Si_(0.33)Ge_(0.67), Si_(0.25)Ge_(0.75) and Si_(0.20)Ge_(0.80), precisely matching those of the corresponding precursors SiH₃GeH₃, (H₃Ge)₂SiH₂, (H₃Ge)₃SiH and (H₃Ge)₄Si.⁸ Our results demonstrate that exact control of the composition, structure and strain at the atomic level can be achieved via incorporation of the entire Si—Ge framework of the precursors into the film. The resulting films are of much higher quality than those previously reported using conventional sources and grow at much lower temperatures that are compatible with CMOS technology.

Within this compositional range the Si_(0.50)Ge_(0.50) semiconductor system is of particular importance because it possesses the ideal lattice dimensions to integrate fully strained Si channels exhibiting high electron mobilities into metal oxide silicon field effect transistors (MOSFETS). Thus these materials are ideally suited for immediate technological applications in high-speed devices. However, in our experiments we have observed that stoichiometric Si_(0.50)Ge_(0.50), with the required device quality properties (surface planarity, low defect densities), can only be grown near a maximum temperature of ˜450° C. at a growth rate of only 0.2 nm/min which is too low to be practical for high throughput device fabrication. Negligible film growth was observed at lower temperatures via H₃GeSiH₃, while films with rough surfaces and high dislocation densities were obtained above ˜500° C. due to the thermal mismatch with the substrate.

The synthesis of new compounds with increased reactivities and improved properties for device fabrication relative to H₃GeSiH₃ would be of great value in the art.

SUMMARY OF THE INVENTION

In one aspect, the present invention provides compounds comprising a silicon-germanium hydride of formula I: SiH_(n1)(GeH_(n2))_(y),

wherein y is 2, 3, or 4;

wherein n1 is 0, 1, 2, or 3 to satisfy valency; and

wherein n2 is independently 0, 1, 2, or 3 for each Ge atom in the compound, to satisfy valency.

In a second aspect, the present invention provides semiconductor structures, comprising a substrate and an Si—Ge layer formed by introducing near the surface of a substrate a gaseous precursor comprising one or more compounds according to formula I.

In further aspect, the invention provides semiconductor structures, comprising a substrate and an Si—Ge layer comprising a backbone of one or more compounds according to formula I.

In a third aspect, the present invention provides methods for synthesizing one or more silicon-germanium hydrides of formula I, comprising combining a compound selected from the group consisting of a nonafluorobutane-sulfonic substituted disilane and a triflate substituted disilane, with a compound comprising a GeH₃ ligand under conditions whereby the silicon-germanium hydride is formed.

In a fourth aspect, the present invention provides methods for depositing a Si—Ge material on a substrate in a reaction chamber, comprising introducing into the chamber a gaseous precursor comprising one or more compounds according to formula I, under conditions whereby a layer comprising a Si—Ge material is formed on the substrate.

In a fifth aspect, the present invention provides methods for depositing an epitaxial Si—Ge layer on a substrate, comprising introducing at or near a surface of the substrate a gaseous precursor comprising one or more compounds of formula I, and dehydrogenating the precursor under conditions whereby epitaxial Si—Ge is formed on the substrate.

DESCRIPTION OF THE FIGURES

FIG. 1: Molecular structure of the conformational isomer pairs {n-GeSiSiGe, g-GeSiSiGe}, {n-GeSiGeGe, g-GeSiGeGe} and positional isomer i-Si(GeSiSi).

FIG. 2: Calculated IR spectra of n-GeSiSiGe, g-GeSiSiGe, and i-Si(GeSiSi). The low- and high-frequency range is shown in panels {(a),(b),(c)} and {(d),(e),(f)}, respectively. Empirical frequency scaling has not been applied to the spectra shown here. Individual spectral features of the n-GeSiSiGe, g-GeSiSiGe and i-Si(GeSiSi) molecules are labeled with “n”, “g” and “i”, respectively. Corresponding molecular structures are drawn as insets in the low-frequency plots.

FIG. 3: Calculated IR spectra of n-GeSiGeGe and g-GeSiGeGe. The low- and high-frequency range is shown in panels {(a),(b)} and {(c),(d)}, respectively. The spectral features of the n-GeSiGeGe and g-GeSiGeGe isomers are labeled “N” and “G”, respectively. Empirical frequency scaling has not been applied to the spectra shown here. Corresponding molecular structures are drawn as insets in the low-frequency plots.

FIG. 4: Comparison of an experimental spectrum of (GeH₃)₂(SiH₂)₂ (1) with a superposition of theoretical spectra for the {n-GeSiSiGe, g-GeSiSiGe} combination: (a) low-frequency region (500-1100 cm⁻¹) and (b) high-frequency Si—H/Ge—H region (1900-2300 cm⁻¹). Frequency scale factors of 0.984 and 0.975 have been applied to the theoretical spectra in low- and high-frequency regions, respectively. The theoretical spectra consist of an admixture of 39% n-GeSiSiGe and 61% g-GeSiSiGe.

FIG. 5: Comparison of an experimental spectrum of a mixture (GeH₃)₂(SiH₂)₂ (1) with a superposition of theoretical spectra for the {i-Si(GeSiSi), g-GeSiSiGe} combination: (a) low-frequency region (500-1100 cm⁻¹) and (b) high-frequency Si—H/Ge—H region (1900-2300 cm⁻¹). Frequency scale factors of 0.985 and 0.976 have been applied to the theoretical spectra in low- and high-frequency regions, respectively. The theoretical spectra consist of an admixture of 68% i-Si(GeSiSi) and 32% g-GeSiSiGe.

FIG. 6: Comparison of an experimental spectrum of (GeH₃)₂(SiH₂GeH₂) (3) with a superposition of theoretical spectra for the {n-GeSiGeGe, g-GeSiGeGe} combination: (a) low-frequency region (500-1100 cm⁻¹) and (b) high-frequency Si—H/Ge—H region (1900-2300 cm⁻¹). Frequency scale factors of 0.985 and 0.976 have been applied to the theoretical spectra in low- and high-frequency regions, respectively. The theoretical spectra consist of an admixture of 23% n-GeSiGeGe and 77% g-GeSiGeGe.

FIG. 7: Relaxed potential energy surface of as a function of the molecular backbone torsion angle for butane (black), tetrasilane (red) and GeSiSiGe (blue). Solid and dashed lines correspond to CCSD/LANL2DZ and B3LYP/6-311G++(3df,2pd) calculations, respectively.

FIG. 8: Temperature dependence of the first layer growth rates for the precursors: H₃GeSiH₃, Ge₂H₆ and (H₃Ge)₂(SiH)₂ (1). The activation energies for these compounds are 1.95, 1.66 and 1.42 eV, respectively.

FIG. 9: XTEM micrographs of a Si_(0.50)Ge_(0.50) layer grown on Si(100) at 350° C. No threading defects are observed within the field of view of ˜2.5 μm, indicating a dislocation density of <10⁶/cm².

FIG. 10: Diffraction contrast, high resolution XTEM micrographs of a Si_(0.50)Ge_(0.50) layer grown on Si(100) at 400° C. The film is nearly strain-free (˜85%) and displays an atomically smooth surface, free of threading defects (top). The mismatch with Si(100) is accommodated by dislocations located at the interface (bottom left). Defects originating at the interface show the propensity to penetrate downward into the Si(100) substrate (bottom right).

FIG. 11: (a) AFM image of Si_(0.50)Ge_(0.50) on Si(100) showing the cross-hatch pattern morphology with an RMS roughness of 2.3 nm. (b) AFM image of a strain-relaxed and completely planar film with an RMS roughness of 0.5 nm.

FIG. 12: Calculated thermochemical (300K) and structural properties of the conformational isomer pairs {n-GeSiSiGe, g-GeSiSiGe}, {n-GeSiGeGe, g-GeSiGeGe} and positional isomer i-Si(GeSiSi). The units for bond lengths, bond angles and energies are Angstroms, degrees and Hartree, respectively.

FIG. 13A-B Exemplary sequence of macromolecular, polymeric units based on interconnected (GeH₃)₂(SiH₂)₂ monomers (a-d), en route to a diamond cubic Si—Ge lattice with concentration Ge₂Si₂ (Si_(0.50)Ge_(0.50)) (e). This material incorporates the Ge—Si—Si—Ge molecular core of (GeH₂)₂(SiH₂)₂ as the structural and compositional building block.

FIG. 14. Hypothetical growth sequence of a two dimensional island of composition Si_(0.50)Ge_(0.50) containing a random distribution of Si and Ge atoms. The schematic process is viewed along the normal to the (111) growth plane, and involves the systematic addition of n-GeSiSiGe molecules and simultaneous abstraction of H₂ molecules. Legend: dark circles—Ge; light circles—Si; small white circles—H.

FIG. 15. Hypothetical growth sequence of a two dimensional island of composition Si_(0.50)Ge_(0.50) containing a random distribution of Si and Ge atoms. The schematic process is viewed along the normal to the (001) growth plane, and involves the systematic addition of n-GeSiSiGe molecules and simultaneous abstraction of H₂ molecules. Legend: dark circles—Ge; light circles—Si; small white circles—H.

DETAILED DESCRIPTION OF THE INVENTION

All publications, patents and patent applications cited herein are hereby expressly incorporated by reference for all purposes.

As used herein, the singular forms “a”, “an” and “the” include plural referents unless the context clearly dictates otherwise.

In one aspect, the present invention provides compounds comprising or consisting of a silicon-germanium hydride of formula I: SiH_(n1)(GeH_(n2))_(y),

wherein y is 2, 3, or 4;

wherein n1 is 0, 1, 2, or 3 to satisfy valency; and

wherein n2 is independently 0, 1, 2, or 3 for each Ge atom in the compound, to satisfy valency.

As used herein, the phrase “to satisfy valency” means to maintain tetra-valency of each Si and Ge atom in the compounds of the invention.

As demonstrated herein, compounds according to formula I can be used, for example, in controlled depositions to produce stoichiometric SiGe films possessing desired properties for semiconductor applications including perfectly crystalline and epitaxial microstructures, smooth morphologies, and uniformly strain-relaxed states. The compounds of formula I are herein demonstrated to be remarkably stable over extended periods of time, and thus represent viable molecular sources for potential industrial applications.

Thus, in one embodiment of this first aspect, y is 2; in an alternative embodiment y is 3; in a further alternative embodiment y is 4.

In certain preferred embodiments, n1 is 1, 2, or 3, to satisfy valency. In these preferred embodiments, if y is 2, then n1 is 1 or 3. In these preferred embodiments, if y is 3 then n1 is 2 or 3.

In certain other embodiments, if y is 3, then n2 is 2 for at least one Ge atom in the compound.

In certain further embodiments, if y is 3, then n1 is 1, or 2.

Compounds according to this aspect of the invention include any conformational form of the compound, including but not limited n, g, and iso-forms of the compounds, and combinations thereof.

Exemplary silicon-germanium hydrides according to this aspect of the invention comprise or consist of those compounds listed in Table 1. All Si and Ge atoms in the compounds are tetravalent. Dashed lines represent bonds between Si and Ge atoms in the linear versions. In the isobutene- and isopentane-like isomers, the Si and Ge atoms inside the brackets are directly bound to the Si or Ge to the left of the brackets; the Si or Ge in parenthesis outside of the brackets at the far right in some of the compounds are directly bound to the last Si or Ge inside of the brackets.

For example, FIG. 1 shows compound n-Ge—Si—Ge—Ge. As noted in Table 1, this compound is also referred to as GeH₃—SiH₂—GeH₂—GeH₃.

TABLE 1 3 and 4 metal variants: (a) Linear SiH₃—GeH₂—GeH₃; Si₁Ge₂H₈ GeH₃—SiH₂—GeH₃ Si₁Ge₂H₈ SiH₃—GeH₂—GeH₂—GeH₃; Si₁Ge₃H₁₀ GeH₃—SiH₂—GeH₂—GeH₃; Si₁Ge₂H₁₀ (b) iso-butane-like SiH[(GeH₃)₃] Si₁Ge₃H₁₀ GeH[(GeH₃)₂(SiH₃)] Si₁Ge₃H₁₀ 5 metal atom variants: (a) Linear: GeH₃—GeH₂—GeH₂—GeH₂—SiH₃ Si₁Ge₄H₁₂ GeH₃—GeH₂—GeH₂—SiH₂—GeH₃ Si₁Ge₄H₁₂ GeH₃—GeH₂—SiH₂—GeH₂—GeH₃ Si₁Ge₄H₁₂ (b) Iso-pentane-like GeH[(SiH₃)(GeH₃)(GeH₂)](GeH₃) Si₁Ge₄H₁₂ GeH[(GeH₃)₂(GeH₂)](SiH₃) Si₁Ge₄H₁₂ GeH[(GeH₃)₂(SiH₂)](GeH₃) Si₁Ge₄H₁₂ SiH[(GeH₃)₂(GeH₂)](GeH₃) Si₁Ge₄H₁₂ GeH[(GeH₃)₂(SiH₂)](GeH₃) Si₁Ge₄H₁₂ Neopentane-like Si[(GeH₃)₄] Si₁Ge₄H₁₂

As noted above, these compounds each include the n or g forms, and stereoisomers thereof.

In a preferred embodiment, the silicon germanium hydride is GeH₃—SiH₂—GeH₂—GeH₃.

This first aspect also provides compositions comprising combinations of the silicon germanium hydrides According to formula I.

In a further embodiment, the compounds of the invention are substantially isolated. As used herein, a “substantially isolated” compound of the invention is one compound, or two or more compounds of the invention in combination, that are at least 75% isolated from precursors and other contaminants, and preferably 80%, 85%, 90%, 95%, 98%, or more isolated.

In a second aspect, the present invention provides semiconductor structures, comprising a substrate; and an Si—Ge layer formed by introducing near the surface of a substrate a gaseous precursor comprising or consisting of one or more silicon-germanium hydride compounds of formula I.

As shown herein, the silicon-germanium hydride compounds of formula I are especially useful for fabricating SiGe semiconductor alloys at unprecedented low temperatures that display homogeneous compositional and strain profiles, low threading dislocation densities and atomically planar surfaces. Controlled depositions have produced stoichiometric SiGe films reflecting the Si/Ge content of the precursor, and possessing the desired properties for semiconductor applications including perfectly crystalline and epitaxial microstructures, smooth morphologies, and uniformly strain-relaxed states.

In this aspect, the substrate can be any substrate suitable for semiconductor or flat panel display use, including but not limited to silicon, germanium, silicon on insulator, Ge:Sn alloys, SiO₂, sapphire, quartz, Si:Ge alloys, Si:C alloys, stainless steel, polyimide or other polymer films such as those used in the fabrication of flexible displays. In a preferred embodiment, the substrate comprises Si(100).

In a preferred embodiment, the semiconductor substrates of this aspect of the invention have an SiGe layer which comprises an SiGe film having a thickness of less than one micron, more preferably a thickness in a range from 50 nm to 500 nm. In a further preferred embodiment, the semiconductor substrates of this second aspect have an SiGe layer comprising an SiGe film having a density of threading defects of 10⁶/cm² or less. In a further preferred embodiment, the semiconductor substrates of this aspect of the invention comprise an SiGe film having a substantially atomically planar surface morphology.

In various embodiments, the gaseous precursor comprises or consists of one or more of the compounds listed in Table 1, each in n or g forms, and stereoisomers thereof.

In a preferred embodiment of the semiconductor substrates of the second aspect, the gaseous precursor comprises or consists of GeH₃—SiH₂—GeH₂—GeH₃.

The semiconductor structure may further comprise other features as desired, including but not limited to the inclusion of dopants, such as boron, phosphorous, arsenic, and antimony. These embodiments are especially preferred for semiconductor substrates used as active devices. Inclusion of such dopants into the semiconductor substrates can be carried out by standard methods in the art.

In a further embodiment, the semiconductor structure may further comprise varying quantities if carbon or tin, as desired for a given application. Inclusion of carbon or tin into the semiconductor substrates can be carried out by standard methods in the art. The carbon can be used to reduce the mobility of the dopants in the structure and more specifically boron. Incorporation of Sn can yield materials with novel optical properties such as direct emission and absorption leading to the formation of Si-based lasers and high sensitivity infrared photodetectors.

In further aspect, the invention provides semiconductor structures, comprising a substrate and an Si—Ge layer comprising or consisting of a backbone of one or more compounds according to the formula I. Preferred embodiments are as described above.

In a further aspect, the invention provides a composition, comprising one or more compounds according to formula I in an inert gas. Such inert gases include, but are not limited to H₂, He, N₂, and argon. Preferred embodiments are as described above.

By using the compounds of formula I as precursors for preparing semiconductor substrates, the semiconductor substrate will comprise an Si—Ge layer comprising or consisting of a backbone of the compounds of the invention. By using the compounds of the invention, as opposed to the separate use of Si and Ge sources for deposition, the resulting Si—Ge layer comprises highly defined and uniform bonding arrangements and strain compensated Si—Ge atomic patterns, as opposed to the random nature of prior Si—Ge films in which the Si and Ge atoms can exist as an intimate mixture of several (or multi) atom Si and Ge clusters leading to inhomogeneous bonding and locally stressed configurations. In mismatched heteroepitaxy applications these materials exhibit copious dislocations (at levels unacceptable for most device applications), strain non-uniformities and high surface roughness. A distinct and important advantage of our compounds, films, and methods over conventional ones is that the incorporation of the entire Si—Ge molecular core promotes the formation of exceptionally uniform bonding arrangements over the entire crystal, leading to relaxed (or uniformly stressed) films with planar surface morphology (no surface ripples). A crucial advantage is the unprecedented low growth temperatures which reduce surface mobility of the Si and Ge atoms and prevent mass segregation thereby resulting in highly uniform compositional and strain profiles at the atomic level.

The intact incorporation of the massive Si/Ge cores into the film also leads to low surface diffusion and high sticking coefficients compared to the conventional low mass compounds. The high reactivity permits promotes high growth rates which increase systematically with the mass of the precursors

Furthermore, the incorporation of the entire Si/Ge framework of the gaseous precursor into the lattice is particularly important in the formations of SiGe nanoscale systems (quantum dots and wires) because it allows precise control of morphology, tunable composition, and structure that cannot be accomplished by vapor deposition of separate silanes and germanes, or by molecular beam epitaxy of solid Si and Ge sources. The precise control of composition and corresponding morphology, both of which ultimately determine the physical properties of these nanoscale materials is a crucial issue. Any compositional variations that exist within and among individual nanostructures will have a significant impact on the optical and electronic properties and on the performance of devices. In the MBE case an average concentration is assigned on the basis of the flux ratio utilized to grow the materials. In the CVD approach the local stoichiometry on the scale of the nanostructure size is even less certain because reactions of various molecular sources cannot be simultaneously controlled at every site throughout the sample. Thus neither technique can guarantee systematic growth of Si—Ge nanoscale structures with controllable composition, strain and size.

Such highly defined patterns can be determined using standard methods in the art, such as neutron diffraction

An example of an Si—Ge layer comprising a backbone of the compounds of the invention can be found in FIG. 13, which shows an exemplary sequence of macromolecular, polymeric units of the invention, based on interconnected (GeH₃)₂(SiH₂)₂ monomers (a-d), en route to a diamond cubic Si—Ge lattice with concentration Ge₂Si₂ (Si_(0.50)Ge_(0.50)) (e). This material incorporates the Ge—Si—Si—Ge molecular core of (GeH₃)₂(SiH₂)₂ as the structural and compositional building block.

FIGS. 14 and 15 illustrate schematically, the molecule-by-molecule growth of a random 2D (one layer) clusters of SiGe film. FIG. 14 shows the hypothetical growth sequence of a two dimensional island of composition Si_(0.50)Ge_(0.50) containing a random distribution of Si and Ge atoms. The schematic process is viewed along the normal to the (111) growth plane and involves the systematic addition of n-GeSiSiGe molecules and simultaneous abstraction of H₂ molecules. FIG. 15 is similar, but the schematic process is viewed along the normal to the (001) growth plane.

As will be understood by those of skill in the art, other macromolecular, polymeric units of the invention, based on one or more other polymerized compounds of the invention can also lead to Si—Ge lattices with a desired concentration of Ge and Si based on the concentration of each in the compound used. Thus, based on the teachings herein, those of skill in the art can prepare similar Si—Ge layers using one or more compounds according to formula I of the present invention.

Thus, the compounds of the invention can be used to form a random alloy with intimate mixing of the elements using the compounds of formula I. The resulting Si—Ge backbone structure consists of polymerized units of the starting compound of the invention, wherein polymerization requires dehydrogenation.

Preferred embodiments of this aspect are as discussed above for the second aspect of the invention.

In a third aspect, the present invention provides methods for synthesizing one or more silicon-germanium hydrides of formula I, wherein the method comprises combining a compound selected from the group consisting of a nonafluorobutane-sulfonic substituted disilane and a triflate substituted disilane, with a compound comprising a GeH₃ ligand under conditions whereby the silicon-germanium hydride is formed.

Thus, this aspect provides methods for making the compounds of formula I. The synthetic routes described herein utilize high yield single-step substitution reactions to yield semiconductor grade materials suitable for industrial application and manufacturing processes.

In one embodiment of this third aspect, the compound comprising a GeH₃ ligand is selected from the group consisting of KGeH₃, NaGeH₃, and MR₃GeH₃, wherein M is a group IV element and R is an organic ligand.

In a further embodiment of this third aspect, the method comprises combining the compound comprising a GeH₃ ligand with a nonafluorobutane-sulfonic substituted disilane, wherein the nonafluorobutane-sulfonic substituted disilane comprises (SO₃C₄F₉)₂(SiH₂)₂. In other embodiments, entire families of perfluoroalkyl sulfonyl and alkyl sulfonyl substituted silanes (or germanes) can be used. More preferably, the compound comprising a GeH₃ ligand is KGeH₃. Even more preferably, the method comprises:

(a) adding (SO₃C₄F₉)₂(SiH₂)₂ to a slurry of KGeH₃ in solvent at between −50° C. and −30° C. (more preferably about −40° C.) to form a mixture;

(b) warming the mixture to between −20° C. and 0° C. (more preferably about −10° C.);

(c) stirring the mixture under nitrogen;

(d) heating the mixture to between 25° C. and 45° C. (more preferably about 35° C.); and

(e) distilling the mixture to form the GeH₃—SiH₂—GeH₂—GeH₃.

In an alternative embodiment of this third aspect, the method comprises combining the compound comprising a GeH₃ ligand with a triflate substituted disilane, and wherein the triflate substituted disilane comprises (SO₃CF₃)₂(SiH₂)₂. More preferably, the compound comprising a GeH₃ ligand is KGeH₃. Even more preferably, the method comprises

(a) adding (SO₃CF₃)₂(SiH₂)₂ to a slurry of KGeH₃ in solvent at between −40° C. and −10° C. (more preferably about −30° C.) to form a mixture;

(b) optionally warming the mixture to between 10° C. and 35° C. (more preferably about 23° C.);

(c) stirring the mixture under nitrogen; and

(d) distilling the mixture to form the GeH₃—SiH₂—GeH₂—GeH₃

In this embodiment, low temperature (T<−10° C.) reactions of (SO₃CF₃)₂(SiH₂)₂ with KGeH₃ afforded predominately (H₃Ge)₂(SiH₂)₂ and impurity levels of (GeH₃)₂(SiH₂GeH₂) (also referred to as GeH₃—SiH₂—GeH₂—GeH₃). These species can be separated by distillation. In contrast to the low temperature pathways, the reaction of (SO₃CF₃)₂(SiH₂)₂ with KGeH₃ at T 22° C. yields predominately combinations of the positional isomers (GeH₃)₂(SiH₂)₂ and (GeH₃)₂SiH(SiH₃) in varying proportions (a small amount of (GeH₃)₂(SiH₂GeH₂) is also produced but this is readily separated form the bulk via fractional distillation from the (SO₃CF₃)₂(SiH₂)₂ and (GeH₃)₂(SiH₂GeH₂) mixture.

In a fourth aspect, the present invention provides methods for depositing a Si—Ge material on a substrate in a reaction chamber, comprising introducing into the chamber a gaseous precursor comprising or consisting of one or more compounds according to formula I, under conditions whereby a layer comprising a Si—Ge material is formed on the substrate.

In a fifth aspect, the present invention provides methods for depositing an epitaxial Si—Ge layer on a substrate, comprising introducing near a surface of the substrate a gaseous precursor comprising or consisting of one or more compounds according to formula I, and dehydrogenating the precursor under conditions whereby epitaxial Si—Ge is formed on the substrate.

In this aspect, the substrate can be any substrate suitable for semiconductor or flat panel display use, including but not limited to silicon, germanium, silicon on insulator, Ge:Sn alloys, SiO₂, sapphire, quartz, Si:Ge alloys, Si:C alloys, stainless steel, polyimide or other polymer films such as those used in the fabrication of flexible displays. In a preferred embodiment, the substrate comprises Si(100).

Embodiments of the gaseous precursors are as described above for previous aspects of the invention. For example, the methods may further comprise adding a dopant on the substrate, including but not limited to the inclusion of dopants, such as boron, phosphorous, arsenic, and antimony. These embodiments are especially preferred for semiconductor substrates used as active devices. Inclusion of such dopants into the semiconductor substrates can be carried out by standard methods in the art.

In another embodiment, the methods comprise adding varying quantities if carbon or tin to the semiconductor substrate. Inclusion of carbon or tin into the semiconductor substrates can be carried out by standard methods in the art. The carbon can be used to reduce the mobility of the dopants in the structure and more specifically boron. Incorporation of Sn can yield materials with novel optical properties such as direct emission and absorption leading to the formation of Si-based lasers and high sensitivity infrared photodetectors.

As demonstrated herein, the silicon-germanium hydrides of the invention were used to deposit device quality layers on substrates that display homogeneous compositional and strain profiles, low threading dislocation densities and atomically planar surfaces.

In a preferred embodiment of the fourth and fifth aspects of the invention, the step of introducing the gaseous precursor comprises introducing the gaseous precursor in substantially pure form. In a further preferred embodiment, the step of introducing the gaseous precursor comprises introducing the gaseous precursor as a single gas source.

In another embodiment of the fourth and fifth aspects, the step of introducing the gaseous precursor comprises introducing the gaseous precursor intermixed with an inert carrier gas. In this embodiment, the inert gas can be, for example, H₂ or N₂.

In these aspects, the gaseous precursor can be deposited by any suitable technique, including but not limited to gas source molecular beam epitaxy, chemical vapor deposition, plasma enhanced chemical vapor deposition, laser assisted chemical vapor deposition, and atomic layer deposition.

In a preferred embodiment of the fourth and fifth aspects, the gaseous precursor is introduced at a temperature of between 300° C. and 450° C., more preferably between 350° C. and 450° C. Practical advantages associated with this low temperature/rapid growth process include (i) short deposition times compatible with preprocessed Si wafers, (ii) selective growth for application in high frequency devices, and (iii) negligible mass segregation of dopants, which is particularly critical for thin layers.

In various further embodiments of the fourth and fifth aspects, the gaseous precursor is introduced at a partial pressure between 10⁻⁸ Torr and 1000 Torr. In one preferred embodiment, the gaseous precursor is introduced at between 10⁻⁸ Torr and 10⁻⁵ Torr (corresponding to UHV vertical furnace technology). In another preferred embodiment, the gaseous precursor is introduced at between 10⁻⁸ Torr and 100 Torr, corresponding to LPCVD conditions.

In various other preferred embodiments, the Si—Ge material is formed on the substrate as a strain-relaxed layer having a planar surface; the composition of the Si—Ge material is substantially uniform; and/or the entire Si and Ge framework of the gaseous precursor is incorporated into the Si—Ge material or epitaxial Si—Ge.

EXAMPLES

The synthesis of butane-like (GeH₃)₂(SiH₂)₂ (Also referred to as GeH₃—SiH₂—SiH₂—GeH₃) (1), (GeH₃)₂SiH(SiH₃) (also referred to as SiH[(GeH₃)₂(SiH₃)] (2) and (GeH₃)₂(SiH₂GeH₂) (referred to above as GeH₃—SiH₂—SiH₂—GeH₃) (3) Si—Ge hydrides with applications in low temperature synthesis of Ge-rich Si_(1-x)Ge_(x) optoelectronic alloys is herein demonstrated. The compositional, vibrational, structural and thermochemical properties of these compounds were studied by FTIR, multinuclear NMR, mass spectrometry, Rutherford backscattering, and density functional theory (DFT) simulations. The analyses indicate that the linear (GeH₃)₂(SiH₂)₂ (1) and (GeH₃)₂(SiH₂GeH₂) (3) compounds exist as a mixture of the classic normal and gauche conformational isomers which do not seem to interconvert at 22° C. The conformational proportions in the samples were determined using a new fitting procedure, which combines calculated molecular spectra to reproduce those observed by varying the global intensity, frequency scale and admixture coefficients of the individual conformers. The (GeH₃)₂(SiH₂)₂ (1) species was then utilized to fabricate Si_(0.50)Ge_(0.50) semiconductor alloys reflecting exactly the Si/Ge content of the precursor. Device quality layers were grown via gas source MBE directly on Si(100) at unprecedented low temperatures 350-450° C. and display homogeneous compositional and strain profiles, low threading dislocation densities and atomically planar surfaces. Low energy electron microscopy (LEEM) analysis has demonstrated that the precursor is highly reactive on Si(100) surfaces, with H₂ desorption kinetics comparable to those of Ge₂H₆, despite the presence of strong Si—H bonds in the molecular structure.

Results and Discussion

The synthesis of the main product 1,2-digermyldisilane, (H₃Ge)₂(SiH₂)₂ (1) was accomplished via reactions of KGeH₃ with the nonafluorobutane-sulfonic and triflate substituted disilanes (C₄F₉SO₃)₂(SiH₂)₂ (4) and (SO₃CF₃)₂(SiH₂)₂ (5) as illustrated by Eq 1 and 2 respectively. The starting materials (4) and (5) were prepared via reactions of the corresponding sulfonic acids HSO₃C₄F₉ and HSO₃CF₃ with 1,2-(p-tolyl)₂(SiH₂)₂ (Eq 3 and 4, respectively). (SO₃C₄F₉)₂(SiH₂)₂+2KGeH₃→(H₃Ge)₂(SiH₂)₂+2KSO₃C₄F₉  (1) (SO₃CF₃)₂(SiH₂)₂+2KGeH₃→(H₃Ge)₂(SiH₂)₂+2KSO₃CF₃  (2) (p-tolyl)₂(SiH₂)₂+2HSO₃C₄F₉→(SO₃C₄F₉)₂(SiH₂)₂+2(toluene)  (3) (p-tolyl)₂(SiH₂)₂+2HSO₃CF₃→(SO₃CF₃)₂(SiH₂)₂+2(toluene)  (4) The route described by (Eq 1) consistently produces pure, single-phase (H₃Ge)₂(SiH₂)₂ (1) as a colorless, pyrophoric liquid. Here the replacement of —SO₃C₄F₉ by GeH₃ occurs exclusively at the 1,2-substitution sites of (SO₃C₄F₉)₂(SiH₂)₂ (4), as expected. However, the route described by (Eq 2) yields a mixture of products (FIG. 2) including (GeH₃)₂(SiH₂)₂ (1), the isobutane analog (GeH₃)₂SiH(SiH₃) (2), and the Ge-rich derivative (GeH₃)₂(SiH₂GeH₂) (3) depending on reaction conditions. Specifically, low temperature (T<−10° C.) reactions of (SO₃CF₃)₂(SiH₂)₂ (5) with KGeH₃ (Eq 2) afforded predominately (1) and impurity levels of (3). These species are separated by distillation and the minor low volatility fraction (vapor pressure of 1 Torr at 22° C.) was characterized by a variety of spectroscopic methods as the Ge-rich derivative (3) possessing a heteronuclear H₂Si—GeH₂ core (FIG. 1). In contrast to the low temperature pathways, the reaction of (SO₃CF₃)₂(SiH₂)₂ (5) with KGeH₃ at T≧22° C. yields predominately combinations of the positional isomers (1) and (2) in varying proportions (a small amount of (3) is also produced but this is readily separated form the bulk via fractional distillation from the (1) and (2) mixture). In this case the replacement of SO₃CF₃ by GeH₃ initially occurs at the 1-substitution site of (SO₃CF₃)₂(SiH₂)₂ (5) as expected. The second replacement likely produces germyl disilane, SiH₃SiH₂GeH₃, and a stable germylene intermediate (GeH₂) rather than the 1,2-digermyldisilane, (H₃Ge)₂(SiH₂)₂ (1). Insertion of GeH₂ into SiH₃SiH₂GeH₃ then may yield (GeH₃)₂SiH(SiH₃) (3) as shown in Eq 6. A similar insertion mechanism (discussed in detail in subsequent sections) has been observed in the photochemical generation of gas phase i-Si₄H₁₀ from SiH₂ insertion into trisilane SiH₃—SiH₂—SiH₃ (Eq 7): —SiH₂—SiH₂—GeH₃+GeH₃→SiH₃—SiH₂—GeH₃+GeH₂→(GeH₃)₂SiH(SiH₃)  (6) SiH₃—SiH₂—SiH₃+SiH₂→(SiH₃)₂SiH(SiH₃)  (7)

The synthesis of (5) is described by (Eq 4) and has been previously demonstrated elsewhere. Its (p-tolyl)₂(SiH₂)₂ starting materials has been produced via coupling reactions of (p-tolyl)SiH₂Cl with powdered lithium.¹⁰ In the present work we adopt a more convenient, analogous approach using readily available sodium fragments as the coupling agent. Compound (5) is obtained as a highly reactive liquid, which is difficult to fully handle and purify. Consequently its reactions with KGeH₃ are complex and produce mixtures of products as described above. In contrast the newly prepared compound (4) is readily crystallized as a robust molecular solid that is completely isolated from the reaction byproducts and other contaminants, thereby leading to high purity (H₃Ge)₂(SiH₂)₂ in subsequent steps according to (Eq 1). The compositional, vibrational and structural properties of the newly synthesized compounds (1), (2), (3) and (4) are presented below.

(H₃Ge)₂(SiH₂)₂ (1):

The (H₃Ge)₂(SiH₂)₂ (1) species is prepared as described by the reactions depicted in (Eq 1, 2) and was isolated and purified by fractional distillation (vapor pressure of ˜8-10 Torr at 22° C.). The FTIR, ²⁹Si NMR (proton-coupled) and mass spectra indicate a 1,2-digermyldisilane with a butane-like structure as shown in FIG. 1. The IR spectrum shows the Si—H and Ge—H stretching modes at 2147 and 2073 cm⁻¹, respectively, and a set of absorption bands between 910 and 442 cm⁻¹ corresponding to the bending modes of the molecule. These assignments are consistent with those made previously for the (H₃Ge)_(4-x)SiH_(x) (x=1-4) family of silyl germanes.⁷ A more detailed interpretation of the full IR spectrum is obtained from quantum chemical calculations and the data show fixed combinations between the butane-like normal and gauche conformers of (1) (see section below for details). The ¹H NMR spectra reveals a quartet at 3.29 ppm and a triplet at 3.11 ppm corresponding to the Si—H and Ge—H protons, respectively, which is consistent with a H₃Ge—SiH₂—SiH₂—GeH₃ molecular structure. This structure is further confirmed with 2D ¹H COSY and ¹H—²⁹Si HMQC NMR experiments. The 2D ¹H COSY spectrum showed cross-peaks that correlate to Si—H and Ge—H resonances at 3.29 and 3.11 ppm, respectively, indicating the H—Si—Ge—H connectivity. A proton-decoupled ¹H—²⁹Si HMQC spectrum showed that the H atoms at 3.29 ppm are directly attached to Si atoms at −105 ppm. The mass spectra revealed an isotopic envelope at 210-196 amu as the highest mass peak corresponding to the parent ion, (Si₂Ge₂H_(x) ⁺). The associated fragmentation pattern is consistent with the proposed structure. The existence of (1) was further corroborated by Rutherford backscattering (RBS) analysis of monocrystalline films produced by single source MBE depositions of the compound at 350° C. (Eq 8). The Si/Ge elemental content of the films was consistently 1:1 reflecting precisely the composition of the Si₂Ge₂ core of the molecule. (H₃Ge)₂(SiH₂)₂ (gas)→2SiGe (film)+5H₂ (gas)  (8) (GeH₃)₂SiH(SiH₃) (2):

The isobutane-like structure of (2) was determined by ²⁹Si and ¹H NMR studies. The proton NMR resonances are present as a multiplet centered at 3.049 ppm due to —SiH, and two doublets centered at 3.213 and 3.404 ppm corresponding to the (—GeH₃)₂ and —SiH₃ protons, respectively. The integrated peak intensity ratios of the —SiH, (—GeH₃)₂ and —SiH₃ are 1:6:3, respectively, as expected. The peak intensities, the coupling patterns and the position of the peaks in the spectrum, collectively point to the isobutane-like structure in which an Si center is tetrahedrally bonded to two GeH₃ groups one SiH₃ group and an single H atom. This structure is further confirmed by 2D ¹H COSY and ¹H—²⁹Si HMQC NMR measurements. The 2D ¹H COSY spectrum showed cross-peaks that correlate to the central SiH, and terminal GeH₃ and SiH₃ resonances at 3.049, 3.213 and 3.404 ppm, respectively, indicating a H₃Si—SiH—(GeH₃)₂ connectivity, which is consistent with the proposed isobutane structure. A proton-decoupled ¹H—²⁹Si HMQC spectrum showed that the H atoms at 3.049 and 3.404 ppm are directly bonded to Si atoms at −121 and −93 ppm, respectively. The ²⁹Si chemical shift (−121 ppm, in C₆D₆) due to the central Si atom in this molecule is similar to those found for SiH(GeH₃)₃ (−113 ppm in CDCl₃) and Si(GeH₃)₄ (−128 ppm, in CDCl₃). A close correspondence is also found between the ²⁹Si chemical shift (−93 ppm) due to the terminal Si atom and those of the terminal SiH₃ groups (−92 ppm) for H₃SiGeH₃.

Gas-chromatography mass-spectrometry experiments (GCMS) of samples containing (1) (H₃Ge)₂(SiH₂)₂ and (GeH₃)₂SiH(SiH₃) (2) indicated the presence of two major fractions that displayed slightly different retention times in the GC column, which is consistent with a mixture of (1) and (2) possessing slightly different boiling points. Furthermore, these fractions displayed essentially identical mass spectra. The highest mass peak is observed in the 210-196 amu range corresponding to the (Si₂Ge₂H_(x) ⁺) parent ions of (1) and (2). Samples of the mixture were further characterized using IR spectroscopy. The spectra are essentially a simple admixture of the individual (1) and (2) components. The spectrum of (2) was theoretically determined since the compound could not be completely separated in pure form from (1) via our distillation method due to the similarity in their boiling points. The contributions of the each compound in the experimental IR spectra were then determined using a fitting procedure involving both the observed and the calculated spectra.

(GeH₃)₂(SiH₂GeH₂) (3):

Compound (3) is a byproduct of the reaction described by Eq 2. Its gas-phase IR spectrum shows the Si—H and Ge—H stretching bands centered at 2145 and 2073 cm⁻¹, respectively. The intensity of the Ge—H peak in the spectrum is significantly stronger than the Si—H due to the greater number of Ge—H bonds relative to Si—H bonds. The ¹H NMR spectra showed a set of two sextets at 3.30 and 3.03 ppm ensconcing two triplets at 3.23, 3.13 ppm. The integrated peak intensity ratios of the sextet-triplet-triplet-sextet sequence are 2:3:3:2. The integrated intensities the coupling patterns and the position of the peaks in the NMR spectrum collectively point to a H₃Ge—SiH₂—GeH₂—GeH₃ molecular structure in which a central SiH₂GeH₂ core is bonded with two terminal GeH₃ moieties. In particular, the sextets at 3.30 and 3.03 ppm can be associated, respectively, with the SiH₂ and GeH₂ protons of the central —SiH₂GeH₂— while the triplets at 3.23, 3.13 ppm correspond to terminal GeH₃ protons. The SiH₂ and GeH₂ NMR frequencies in this case correlate well with those in the previously reported (H₃Ge)₂SiH₂ and GeH₃GeH₂SiH₃ compounds.⁷ The assignment of the sextet at 3.30 ppm to the SiH₂ protons was further corroborated by a ¹H—²⁹Si HMQC NMR spectrum, which indicates a direct coupling to a single ²⁹Si resonance found at −98.2 ppm. In addition, a 2D ¹H COSY NMR spectrum was used to unequivocally establish the specific ordering of the Ge—Si—Ge—Ge backbone constituents. Cross-peaks correlate an Si—H and three Ge—H resonances at 3.30, 3.23, 3.13 and 3.03 ppm. These correspond, respectively, to SiH₂, GeH₃ (terminal) connected to GeH₂, Ge—H₃ (terminal) connected to SiH₂, and GeH₂. The mass spectra showed an isotopic envelope at 256-238 amu as the highest mass peak corresponding to the parent ion, (SiGe₃H_(x) ⁺) and a fragmentation pattern consistent with the molecular structure.

(C₄F₉SO₃)₂(SiH₂)₂ (4):

Compound (4) is isolated at 95% yield as a colorless, pyrophoric solid with a melting point of 68° C. It is readily soluble in ethers, CHCl₃, CH₂Cl₂ and slightly soluble in toluene. The ¹H NMR spectrum showed a singlet centered at 5.08 ppm (δ Si—H) due to SiH₂ and ²⁹Si satellite peaks. These exhibit a triplet of triplets with a 1-bond Si—H coupling of 272 Hz and a H—H 3-bond coupling of 3.6 Hz. This indicates the presence of a second SiH₂ group consistent with the —SiH₂SiH₂— core. Furthermore, a proton decoupled ¹H—²⁹Si HMQC showed that the proton resonance at 5.08 ppm is directly attached to a Si atom at −30.1 ppm. These values are consistent with those observed for the triflate analog (SO₃CF₃)₂(SiH₂)₂ (5).¹⁰ Compound (4) was further characterized by FTIR, mass spectrometry and C, H, F elemental analysis and the data are fully consistent with the proposed structure (see experimental section).

Ab Initio Simulations of Molecular Properties

Structural and Thermochemical Properties:

In order to corroborate the identification of the (GeH₃)₂(SiH₂)₂, (GeH₃)₂SiH(SiH₃) and (GeH₃)₂(SiH₂GeH₂) described above we simulated the structural, energetic and vibrational trends of these compounds. In prior studies⁷ we demonstrated that B3LYP hybrid density functional theory (DFT) simulations provide an excellent account of the ground state structural, thermochemical and vibrational properties of the (H₃Ge)—SiH_(4-x) family of molecular hydrides. In particular use of the 6-311G++(2d,2p) basis set yielded small typical bond length and frequency discrepancies (on the order of 0.4% and 1.4%, respectively). Accordingly, our first attempt at reconciling the observed IR spectra with those calculated was based on the same procedure, and on the assumption that the fundamental structures are n-butane like. Although this approach provided a close match to most of the main spectral features observed, several strong low-frequency features remained unaccounted for in the calculated IR pattern. In view of the prior success of B3LYP approach we concluded that n-butane like molecular structures alone could not account for the spectrum of the synthesized compounds. We therefore expanded our calculations to include the gauche conformational isomers in which a terminal GeH₃ group is rotated out of the Ge—Si—Si—Ge (or Ge—Si—Ge—Ge) skeletal plane, as well as the iso-butane like positional isomer i-Si(SiGeGe) (FIG. 1). These isomers are completely analogous to those previously reported in tetrasilane, and related molecules, and in subsequent discussion we simply refer to them as n-GeSiSiGe, g-GeSiSiGe, n-GeSiGeGe and g-GeSiGeGe, and i-Si(SiGeGe), as shown in FIG. 1. Our results indicate that the observed spectra of both the primary products and the minor impurity compounds are completely accounted for by a linear admixture of the n-, g-, and i-type conformations.

Initial basis set convergence tests showed that a full resolution of differences in the calculated properties of the conformational/positional isomers requires an even more stringent treatment than that used in the prior studies on (H₃Ge)_(x)SiH₄, hydrides, particularly with regards to calculated vibrational properties. Accordingly all of the calculations described in the present work were carried out at the B3LYP/6-311G++(3df,2pd) level as implemented in the Gaussian03 code.¹¹

The results of the structural optimizations, obtained using “tight” convergence criteria, are presented in FIG. 12. The figure lists the bond length, bond angle and bond torsion data for n-GeSiSiGe, g-GeSiSiGe, n-GeSiGeGe, g-GeSiGeGe and i-Si(SiGeGe). In all molecules, the skeletal structure exhibits typical Si—Si and Si—Ge bonds with the gauche conformations exhibiting slightly (0.002 Å) longer/shorter Si—Si/Si—Ge bonds than their linear counterparts. In the iso-butane like isomer i-Si(SiGeGe) the Si—Si bond lengths (2.351 Å) are found to be intermediate to those in the other isomers while the Si—Ge bond is dilated to a value 2.400 Å. All the Si—Si values, 2.350-2.352 Å, correspond closely (˜0.1%) to that found in bulk silicon a√{square root over (3)}/4=2.352 Å where a (5.431 Å) is the lattice constant of crystalline Si in the diamond structure. The Ge—Ge values found in n-GeSiGeGe and g-GeSiGeGe, 2.446 Å, is also close to that of bulk germanium (2.449 Å). The heteronuclear skeletal Si—Ge bond lengths exhibit a distribution in the range 2.396-2.400 Å and represent an average of the Si—Si and Ge—Ge values (2.399 Å).

The Si—H and Ge—H bond lengths occur exclusively as central SiH₂ moieties and terminal GeH₃ groups in the n- and g-GeSiSiGe isomers, with values of 1.486 Å and 1.539 Å, respectively. In the corresponding GeSiGeGe isomers the Si—H bonds associated with the SiH₂ moiety has essentially the same value, 1.485 Å, while the GeH₂ moiety exhibits a slightly longer Ge—H bond (1.542-1.548 Å) than in a GeH₃ terminal group, as expected. Due to its unique structure the i-Si(SiGeGe) isomer possesses both terminal SiH₃ and GeH₃ groups and a single SiH moiety. Here the Ge—H bond lengths associated with the terminal GeH₃ groups have the same value (1.539 Å) as in GeH₃ groups of other isomers, while the corresponding terminal group Si—H₃ bond lengths are slightly contracted (1.483 Å). The longest Si—H bond length is associated with the central SiH moiety and has a value 1.488 Å. Collectively, these bond length trends are consistent with those found previously in the heaviest members of the (H₃Ge)_(N)SiH_(4-N) (N=3, 4) family of molecules.

The data presented in FIG. 12 also shows that the inter-metallic skeletal bond angles, as well as those involving hydrogen-metal bonds, are essentially unchanged between all isomers studied. The only exception is found in the H—Ge—Si bond distributions, which possess several values in the linear n-GeSiSiGe isomer and a unique value in all of the others. The Ge—Si—Si—Ge bond torsion in the linear molecules is 180°, indicating that the metal atoms are confined to a common plane, while the gauche conformations exhibit torsion angles of 66° and 64° in Ge—Si—Si—Ge and Ge—Si—Ge—Ge, respectively. It is also evident from the data that the inter-metallic and metal-hydrogen bond lengths in the i-Si(SiGeGe) isomer are, on average, closer to ideal tetrahedral values than those predicted for the other conformational/positional isomers.

FIG. 12 also lists the thermochemical energies of the molecules, including the total ground state electronic energy E₀, and its value corrected for zero point energy correction (E_(ZPE)), thermal energy (E_(CORR)), enthalpy (H_(CORR)) and free energy (G_(CORR)) at 298K. In the case of the Ge₂Si₂H₁₀ molecules our calculations indicate that i-Si(SiGeGe) isomer is slightly favored at room temperature, with a free energy difference of 0.0008 Hartree or about 2.0 kJ/mol (note: k_(B)T @ 300K˜2.4 kJ/mol) relative to n-GeSiSiGe. The latter molecule's free energy is, in turn, more stable than that of g-GeSiSiGe by about 2.8 kJ/mol. For the GeSiGeGe impurity compound the n-GeSiGeGe isomer free energy is lower than that of its gauche conformation by 0.0020 Hartree (5.3 kJ/mol).

Vibrational Spectra:

In order to facilitate the interpretation of the observed FTIR spectra we calculated the vibrational frequencies and intensities of the conformational isomers n-GeSiSiGe and g-GeSiSiGe, and positional isomer i-Si(SiGeGe) of the primary product, as well as those of the minor species n-GeSiGeGe and g-GeSiGeGe, using the B3LYP DFT functional at the B3LYP/6-311G++(3df,2pd) level. No symmetry was imposed in the calculation of the frequency spectra and all molecules studied exhibited a positive definite spectrum of harmonic frequencies indicating that the ground state structures are dynamically stable.

Ge₂Si₂H₁₀ Molecules:

FIG. 2 shows plots of the calculated spectra of n-GeSiSiGe, g-GeSiSiGe and i-Si(SiGeGe), convoluted with a Gaussian of width ˜20 cm⁻¹ to simulate experimental broadening. Both the high- and low-frequency regions are shown. It should also be noted that frequency scaling typically employed to reconcile the slight frequency overestimates obtained using this level of theory, has not been applied to the calculated spectra shown in these plots. The interpretation of the high-frequency spectral features (FIG. 2) is straightforward: the lower frequency pairs of peaks designated n₆ and n₇ in n-GeSiSiGe (FIG. 2( d)), g₁₁ and g₁₂ in g-GeSiSiGe (FIG. 2( e)), and i₁₁ and i₁₂ in i-Si(SiGeGe) (FIG. 2( f)), correspond to symmetric and anti-symmetric Ge—H stretching vibrations, respectively. Similarly, the symmetric and anti-symmetric Si—H stretching vibrations are designated n₈ and n₉ in n-GeSiSiGe (FIG. 2( d)), g₁₃ and g₁₄ in g-GeSiSiGe (FIG. 2( e)), and i₁₄ and i₁₅ in i-Si(SiGeGe) (FIG. 2( f)), respectively. The calculated splitting (13-14 cm⁻¹) between the symmetric and anti-symmetric bands (in either Si—H or Ge—H) is approximately the same in all isomers, however, all of these bands are systematically lower (˜4-5 cm⁻¹) in frequency in the gauche isomer. In addition to these features the high-frequency spectrum of the positional isomer i-Si(SiGeGe), shown in FIG. 2( f), also exhibits an isolated vibrational feature near 2077 cm⁻¹ (designated by i₁₃ in FIG. 2( f)), which corresponds to the central Si—H stretching vibration.

The low-frequency non-skeletal vibrational structure, also shown in FIG. 2, is considerably more complex and involves in- and out-of-plane, symmetric and antisymmetric Si—H/Ge—H wagging vibrations. The most striking difference between the spectra of n-GeSiSiGe and g-GeSiSiGe (parts (a) and (b) of FIG. 2, respectively) is that four distinct features (n₂-n₅) of the linear isomer are effectively split in its gauche counterpart. For example, the strongest band in n-GeSiSiGe, n₂, corresponding to highly symmetric Si—H wagging vibrations parallel with the molecular backbone, is split into three bands denoted by g₃, g_(s) and g_(s) in the gauche isomer exhibiting very strong Si—H wagging parallel to the Si—Si bond. Among these g₅ involves the least “crowded” protons in the molecule and accordingly exhibits the greatest intensity. The weak shoulder indicated by g₄ in the g-GeSiSiGe spectrum is the anti-symmetric counterpart to mode g₅. Finally, the distinct feature near 925 cm⁻¹ in the n-GeSiSiGe, n₅, corresponds to Si—H wagging vibrations perpendicular to the Si—Si axis involving symmetric H—Si—H bending motion. In the gauche isomer this band is split into symmetric and anti-symmetric counterparts denoted by g₉ and g₁₀. Only a few bands appear to be common to both isomers. In particular features (n₁:g₁) near 430 cm⁻¹ (asymmetrical wagging of the terminal Ge—H protons), (n₃:g₇) near 800 cm⁻¹ (symmetrical terminal Ge—H wagging parallel to the Si—Si bond) and (n₄:g₈) near 876 cm⁻¹ (terminal Ge—H wagging perpendicular to the Si—Ge bonds). The weak band designated g₂ in the FIG. 2( b) involves symmetrical terminal Ge—H wagging, and has a silent counterpart in the n-GeSiSiGe molecule.

The low-frequency spectrum of i-Si(SiGeGe), shown in FIG. 2( c), has a slightly simpler structure due the molecule's higher symmetry. The lowest frequency wagging modes found in the g-GeSiSiGe {g₁, g₂} are effectively split into asymmetrical pairs {i₁,i₂}, and {i₃,i₄}, respectively, in i-Si(SiGeGe). The dominant features near 800 cm⁻¹ (i₇ and i₈) correspond to in-phase and anti-phase symmetrical Ge—H wags of the terminal GeH₃ groups while feature i₉ is the asymmetrical analog to these vibrations. In the SiH₃ terminal group the Si—H wagging vibrations (i₁₀) occur at 951 cm⁻¹. Finally, features i₅ and i₆ are unique to the i-Si(SiGeGe) molecule, and involve perpendicular Si—H wags of the SiH moiety.

SiGe₃H₁₀ Molecules:

For the n- and g-(GeH₃)₂(SiH₂GeH₂) isomers we corroborate the NMR characterization by directly comparing the observed IR spectrum with that calculated for a ˜1:3 mixture of n-GeSiGeGe and g-GeSiGeGe conformations (a detailed explanation is given in the following section). The calculated IR spectra for both the n- and g-isomer, convoluted with a Gaussian of width ˜20 cm⁻¹ to simulate experimental broadening, are given in FIG. 3. Both the high- and low-frequency regions are shown (no frequency scaling has been applied). Peaks in the simulated spectrum originating from n-GeSiGeGe or g-GeSiGeGe conformations are denoted by N_(i) and G_(i), respectively.

The high-frequency Si—H stretching bands are similar to those found in the GeSiSiGe analogs, exhibiting calculated splitting of 13-14 cm⁻¹ between the symmetric and anti-symmetric bands and a systematic overall 4-5 cm⁻¹ shift to lower frequency in the gauche isomer. Here (N₁₁:G₁₇) and (N₁₀:G₁₆) correspond to asymmetric and symmetric Si—H stretches, respectively. However, a simple comparison for corresponding Ge—H stretching vibrations for these isomers is vitiated by the lower symmetry of GeSiGeGe isomers. For example the asymmetrical Ge—H stretch (N₉) in n-GeSiGeGe is split into contributions G₁₂, G₁₄ and G₁₅ in the gauche isomer while the symmetric Ge—H stretch, N₃ in the n-GeSiGeGe, is split into bands G₁₁ and G₁₃.

In the low-frequency range of the spectrum we find a strong correspondence between mode assignments of the n- and g-isomers above 700 cm⁻¹. Specifically, the asymmetrical H—Si—H wagging vibrations N₃ in n-GeSiGeGe appears as G₆ in g-GeSiGeGe, with a frequency near 731 cm⁻¹. As in our earlier discussion we designate such corresponding pairs between isomer conformations as (N₃:G₆). Intense Ge—H wagging vibrations (N₄:G₇) associated with terminal GeH₃ groups appear near 808 cm⁻¹. Similarly, H—Ge—H “scissor” modes at 866 cm⁻¹ are designated as (N₅:G₈), while their H—Si—H counterparts (N₇:G₁₀) appear at 936 cm⁻¹ (the frequency of the corresponding mode in the GeSiSiGe isomers was ˜925 cm⁻¹). The features denoted (N₆:G₉) consist of asymmetrical “scissor”-like vibrations associated with the terminal GeH₃ groups.

The most significant differences between the IR spectra of the n- and g-isomers are found below 700 cm⁻¹. The most intense spectral feature in n-GeSiGeGe (N₂) is associated with a highly symmetric wagging of the protons bound to the GeH₂ moiety parallel to the molecular backbone. In the gauche isomer this mode is split into three features denoted G₃, G₄ and G₅, corresponding to asymmetrical Ge—H wagging of combinations of individual protons in the GeH₂ moiety. Finally, the mode N₁ in the n-isomer, consisting of concerted symmetrical wagging of terminal GeH₃ protons at both ends of the molecule, is split into two modes G₁ and G₂ in the gauche isomer in which symmetrical wagging occurs independently in the two GeH₃ terminal groups.

Isomer Admixture Analysis:

To estimate the molar concentration of the comformational and positional isomers in the observed spectra, we adopt an approach commonly employed in “multi-phase” fitting of x-ray spectra, in which a normalized admixture, of known pure-phase candidate spectra is fitted to an unknown observed spectrum of the combined molecules. Using the same procedures as in our prior studies on Si—Ge hydrides we have calculated the spectra of 10 digermyl-disilyl positional/conformational isomers (to be described elsewhere). These calculated spectra serve as a proxy for the unknown pure isomer candidate spectra normally supplied by experiment. A comparison of our calculated spectra with that of the synthesized compounds suggests the presence of simple admixtures of conformational {n-GeSiSiGe, g-GeSiSiGe} and positional {i-Si(SiGeGe), g-GeSiSiGe} isomers for the Si₂Ge₂H₁₀ family. To proceed with the analysis all of the required theoretical spectra (n-, g- and iso-isomers, see FIG. 2) are first calculated on a fine frequency grid (1 cm⁻¹ spacing), and then partitioned into low-frequency (0-1600 cm⁻¹) and high-frequency (1600-2600 cm⁻¹) regions. We denote the low-frequency spectra of the {n-GeSiSiGe, g-GeSiSiGe} pair by {I_(n)(ω), I_(g)(ω)} and those of {i-Si(SiGeGe), g-GeSiSiGe} by {I_(i)(ω)), I_(g)(ω)}. The corresponding observed spectrum of the synthesized compound, I_(exp)(ω), produced on a discrete frequency grid {ω_(k)} by the spectrometer, is then used to construct an objective function (Eq 9). For example, in the case of the {n-GeSiSiGe, g-GeSiSiGe} admixture:

$\begin{matrix} {{O\left( {\beta,\gamma,\eta} \right)} = {\sum\limits_{k}\left\{ {{I_{{ex}\; p}\left( \omega_{k} \right)} - {\beta\left\lbrack {{\gamma\;{I_{n}\left( {\eta\;\omega_{k}} \right)}} + {\left( {1 - \gamma} \right){I_{g}\left( {\eta\;\omega_{k}} \right)}}} \right\rbrack}} \right\}^{2}}} & (9) \end{matrix}$ where γ is the normalized admixture of n- and g-spectra, β is the global amplitude of the theoretical spectrum and η is the common frequency scale factor applied to the theoretical spectra. An identical procedure is used to treat the {i-Si(SiGeGe), g-GeSiSiGe} combination. In all cases the theoretical spectra were evaluated at arbitrary frequencies using cubic splines, and a robust simplex method was used to minimize the objective function. For the {n-GeSiSiGe, g-GeSiSiGe} pair this yields a scale factor of η=0.984 and an admixture of γ=0.392 (i.e., ˜39% n-GeSiSiGe). This optimized scale factor is very similar to the value 0.989 used in previous studies of the (H₃Ge)—SiH_(4-x) hydrides⁷ and Si₂H₆, Ge₂H₆ and H₃GeSiH₃ molecules¹² at this level of theory. As shown in FIG. 4( a) the resulting low-frequency composite theoretical spectrum (ω<1600 cm⁻¹), generated using this scale factor, agrees remarkably well with the observed one. To simulate the composite high-frequency spectrum for {n-GeSiSiGe, g-GeSiSiGe} we employ the admixture parameter derived from low-frequency behavior, γ=0.392, and reduce the scale factor to η′=(0.9909η)=0.975. This low- to high-frequency scale factor ratio was previously found to yield an excellent account of the scaling behavior in related molecules¹². FIG. 4( b) demonstrates that the optimized parameters obtained using fits to the low-frequency spectra also faithfully and independently reproduce the high-frequency behavior, confirming the integrity of our procedure. Application of the foregoing low-frequency analysis to the positional isomeric combination {i-Si(SiGeGe), g-GeSiSiGe} yields γ=0.985 and γ=0.678 (i.e., ˜68% i-Si(SiGeGe). The sample spectrum is compared with the calculated admixture in FIG. 5, which indicates that the vibrational structure is largely accounted for using the admixture procedure.

The corresponding results for the GeSiGeGe impurity compound are shown in FIG. 6. A completely analogous fitting procedure to that above yields, in this case, an admixture parameter γ=0.235 (i.e., 23.5% n-GeSiGeGe) indicating that the gauche conformation (g-GeSiGeGe) is dominant in the gas phase. As in the GeSiSiGe analysis, we find that fitting parameters obtained from the low-frequency spectrum (ω<1600 cm⁻¹) yields an excellent account of the high-frequency stretching bands using the reduced frequency scale factor 0.975 (FIG. 6( b)).

We have observed that the proportions derived for the conformational isomers are essentially constant between different samples. To elucidate this observation we calculated the potential energy surface (PES) of the butane-like GeSiSiGe as a function of the Ge—Si—Si—Ge backbone torsion angle. The linear conformation corresponds to a torsion angle of 180° while the gauche modification occurs at ˜66° (see FIG. 12). For each fixed value of the torsion angle all remaining structural degrees of the freedom are optimized resulting in a “relaxed” PES. FIG. 7 compares the torsional PES for butane, tetrasilane and GeSiSiGe at the DFT B3LYP/6-311G++(3df,2pd) and ab initio CCSD/LANL2DZ levels of theory. In all cases the value of the linear or trans-configuration is chosen as the reference energy. The plots reveal that all three molecules exhibit very similar energy-torsion profiles with a global minimum at 180°, a n-g barrier (E_(n-g)) at ˜120°, a local minimum at the gauche configuration (E_(g)) near 66° and a maximum value corresponding to the eclipse saddle point (E_(e)). Using the DFT B3LYP/6-311G++(3df,2pd) description we obtain ΔE_(n-g)=0.942, ΔE_(g)=0.362 and ΔE_(e)=1.628 kcal/mol for GeSiSiGe, while the corresponding tetrasilane values are 0.895, 0.360 and 1.591 kcal/mol, respectively. At this level of theory the conformational energy structure of GeSiSiGe and butane-like tetrasilane is essentially identical. This is not unexpected in view of their very similar bond character. At the same level of description we find that the analogous PES for butane shares the same qualitative form as that of tetrasilane and GeSiSiGe, but with significantly larger rotational barriers ΔE_(n-g)=3.235, ΔE_(g)=0.884 and ΔE_(e)=5.713 kcal/mol.

It should be noted that our B3LYP/6-311G++(3df,2pd) tetrasilane values for ΔE_(n-g) and ΔE_(e) are qualitatively different from those calculated by Albinsson et al¹³ at the MP2/6-31* level for the same molecule. In particular the latter authors predict a symmetric n-g barrier and a near identity of gauche and linear conformation energy (ΔE_(n-g)˜0.588, ΔE_(g), ˜−0.04 and ΔE_(e)˜1.236 kcal/mol). Unfortunately, because the basis set levels and model chemistries in our two approaches both differ, the origin of this discrepancy is ambiguous. We therefore carried out a series of coupled cluster calculations at the CCSD/LANL2DZ level for the sequence butane, tetrasilane and GeSiSiGe. The results, shown as solid lines in FIG. 7, are remarkably consistent with the B3LYP-based DFT calculations (dashed lines in the figure), and indicate that the linear butane-like conformation is the ground state structure, with a gauche value of ΔE_(g)˜0.2-0.4 kcal/mol. Furthermore, the magnitude of the barrier connecting the gauche and linear conformations in GeSiSiGe is reduced to 0.36 kcal/mol (˜188 K) in the CCSD/LANL2DZ calculations. This small value of the torsional barriers in tetrasilane and GeSiSiGe is consistent with the facile low-temperature conformational interconversions observed experimentally.

It should be noted that the 68% value obtained for the positional isomeric spectrum, shown in FIG. 5, is characteristic of one particular sample. Unlike the conformational isomers, which exhibited a constant proportion between samples, the proportions of the positional isomers sensitively depend on the specific reaction conditions. This suggests that once the {i-Si(SiGeGe), g-GeSiSiGe} mixture has been isolated no inter-conversion between positional isomers occurs. Chain cleavage and spontaneous isomerization are observed in the closely related tetrasilane Si₄H₁₀ system during photochemical matrix isolation experiments producing trisilane (Si₃H₈) and silylene (SiH₂).¹³ The formation i-Si₄H₁₀ observed as a mixture with n-Si₄H₁₀ is then believed to follow from SiH₂ insertion into the Si—H bonds of trisilane. As discussed in detail by Jasinski et al. this insertion reaction is one of the characteristic mechanisms in gas phase polysilane chemistry, possessing a slight negative activation energy and a very high collisional efficiency.¹⁴ We surmise that an analogous low energy germylene insertion reaction channel is present in our synthesis route (see Eq. 2) involving the triflate-substituted disilanes at T>22° C., leading to the condensation of i-Si(SiGeGe). One plausible mechanism could involve the replacement of —SO₃CF₃ by GeH₃ at the 1-substitution site of (SO₃CF₃)₂(SiH₂)₂ (5), followed by insertion of GeH₂ in the Si—H bonds of the central SiH₂ site in the —SiH₂—SiH₂—GeH₃ intermediate.

Deposition Studies

The deposition experiments were conducted on a clean Si(100) substrates in ultra-high vacuum system equipped with a low energy electron microscope (LEEM) that allowed in situ real time observation of the growth process. The (H₃Ge)₂(SiH₂)₂ gaseous precursor reacted on the Si surface via complete H₂ elimination at partial pressures in the range of 10⁻⁵-10⁻⁸ Torr. Initially, the reaction growth kinetics was investigated using LEEM and the activation energy (E_(act)) of the compound with respect to H₂ desorption from the Si surface was measured. It is known that for conventional silanes and germanes the E_(act) is much lower on a Ge containing surface (including Si_(1-x)Ge_(x)) than on pristine Si. Thus, an accurate determination of E_(act) can only be obtained from measuring the growth rate of the first monolayer, (which grows directly on pure Si) and not that of subsequent layers, which grow on Ge containing surfaces and have higher growth rates. In this regard LEEM is particularly unique because its dynamic imaging differentiates the Si(001)-(2×1) surface from the Si_(1-x)Ge_(x) epilayer and thus provides unambiguous means for the correct determination of E_(act) on Si by measuring the growth rate of the first Si_(1-x)Ge_(x) monolayer vs. temperature.

For comparison the growth rates of Ge₂H₆ and H₃GeSiH₃ were also determined using the same method. For these and for (H₃Ge)₂(SiH₂)₂ the first monolayer took longer to complete on pristine Si than subsequent monolayers. FIG. 8 is a graph showing plots of the temperature dependence of the first layer growth rates. The activation energies were determined using the relation R˜exp(−E_(a)/kT). The data are consistent with the first-order H₂ desorption kinetics and yield E_(act) of 1.95, 1.66 and 1.42 eV, for H₃GeSiH₃, Ge₂H₆ and (H₃Ge)₂(SiH₂)₂, respectively. This indicates that the latter it is not only more reactive than H₃GeSiH₃, but is also more reactive than pure Ge₂H₆ despite the presence of strong Si—H bonds in the molecular structure. Accordingly, it represents a unique high-reactivity species suitable for low temperature (300-400° C.) rapid growth of thick layers (100-500 nm) with stoichiometry Si_(0.50)Ge_(0.50) reflecting that of the corresponding precursor. Below we describe the deposition procedure and key results regarding morphology, microstructure, composition and strain for the films.

The synthesis of Si_(0.5)Ge_(0.5) films was investigated in the 350° C.-500° C. range via dehydrogenation of (H₃Ge)₂(SiH₂)₂. The highest temperature that yields planar layers is ˜450° C. The growth rate is ˜4 nm/min and decreases to 2 nm/min at 350° C. No appreciable growth was observed below 300° C. (1×10⁻⁵ Torr) due to the reduced reactivity of the compound. Thick films with rough surfaces and defective microstructures were produced at 500° C. with growth rates as high as 15 nm/min. The composition and heteroepitaxial character of the films were investigated by random and channeling Rutherford backscattering (RBS), which in all cases indicate a highly stoichiometric material aligned with the substrate. The ratio of the aligned versus the random peak heights (χ_(min)), which measures the degree of crystallinity, decreases from 15% at the interface to 6% at the surface indicating a dramatic reduction in dislocation density across the thickness of the film. This is confirmed by high resolution XTEM, which revealed commensurate SiGe/Si interfaces and perfectly monocrystalline layer microstructures. A survey of TEM samples showed no defects penetrating through the layers within a field of view of ˜2.5 μm in the micrographs indicating an upper limit in the threading dislocation density of ˜10⁶/cm² (FIG. 9). Most of the defects due to the lattice mismatch are concentrated near the interface region. In fact, a number of these appear to originate at the SiGe/Si interface and show a propensity to propagate downward into the substrate (FIG. 9). Occasional edge dislocations spaced by ˜150 nm are also observed in the vicinity of steps on the Si surface (FIG. 10). These are parallel to the interface plane and may provide stress relief between the film and the substrate. The presence of edge dislocations is unusual since SiGe-based materials typically display (111)-threading dislocations and stacking faults. X-ray diffraction (XRD) revealed highly aligned layers with mosaics spreads as low as 0.1 degrees and relatively strain free microstructures. Raman scattering experiments conducted with several Ar+ laser lines revealed a high degree of vertical uniformity in concentration and strain.⁸ The Raman analysis indicated that the composition agrees well with the RBS value and that the strain relaxation is 75% and 95% for films with thickness of 200 and 500 nm, respectively which similar to those obtained by XRD.

Atomic force microscopy (AFM) studies show that films with thickness of 50 and 750 nm display RMS values of 0.5 and 1.5 nm, respectively, for 10×10 μm² areas, indicating highly planar surfaces for samples grown at T<450° C. as shown FIG. 11( a). For layers grown at T>450° C. the AFM images [FIG. 11( b)] show a classic “cross hatched” surface pattern caused by misfit dislocations produced during strain relaxation. It has been shown that both defect induced interface and bulk alloy scattering considerably reduces the electron mobilities in these samples and degrades the device performance.¹⁵ Nevertheless conventional CVD at ultra low pressure is known to produce Si_(1-x)Ge_(x) materials with significantly lower cross hatching patterns leading to higher quality electrical properties. In contrast to these methodologies, which typically involve low-order silanes and germanes (SiH₄, Si₂H₆, GeH₄, Ge₂H₆), the present route utilizes the highly reactive and more massive (H₃Ge)₂(SiH₂)₂ compound. The direct incorporation of the Si₂Ge₂ molecular unit into the film leads to low surface diffusion compared to the conventional low mass compounds. Furthermore, the high reactivity permits low growth temperature and promotes high growth rates at pressures of ˜10⁻⁵ Torr leading to device quality films devoid of cross hatched surface morphologies.

The thermal properties of the films were investigated between 450° C. and 750° C., a range well within device processing temperatures. The XRD lattice constant, the RBS χ_(min) values, and the AFM roughness were measured for the annealed samples and compared with the corresponding values of the as-grown materials. Samples with a thickness as low as 200 nm did not show any increase in surface roughness even after annealing at 750° C. indicating that the surface planarity of our samples is thermally robust. The XRD and RBS aligned spectra were essentially identical before and after annealing. This result also confirms full relaxation in the as-grown layers at T<450° C.

Conclusion

We have demonstrated the synthesis of the butane-like compounds with molecular formulas (GeH₃)₂(SiH₂)₂ (1) (GeH₃)₂SiH(SiH₃) (2) and (GeH₃)₂(SiH₂GeH₂) (3) and their conformational isomers. Detailed characterization of the products was conducted via a range of spectroscopic and analytical methods including quantum chemical simulations. A new fitting procedure was developed, based on the admixture of normal and gauche calculated spectra, to obtain the proportions of the individual conformers in the product sample at 22° C. Controlled depositions of (1) have produced stoichiometric SiGe films possessing the desired properties for semiconductor applications including perfectly crystalline and epitaxial microstructures, smooth morphologies, and uniformly strain-relaxed states. Unique practical advantages associated with this low temperature 350-450° C.) rapid growth include: (i) short deposition times compatible with preprocessed Si wafers, (ii) selective growth for application in high frequency devices, and (iii) negligible mass segregation of dopants, which is particularly critical for thin layers. Finally we have found that these compounds are remarkably stable over extended periods of time, with evidence of decomposition, and thus represent viable molecular sources for potential industrial applications.

Experimental Section

All manipulations were carried out under inert conditions using standard Schlenk and drybox techniques. Dry, air-free solvents were distilled from either anhydrous CaCl₂ or sodium benzophenone ketyl prior to use. All NMR spectra were collected either on a Varian INOVA 400 spectrometer operating at 400 MHz or a Gemini 300 spectrometer. Samples were dissolved in CDCl₃ or C₆D₆ and all nuclei were referenced either directly or indirectly to the proton signal of TMS or the residual solvent peak as indicated. IR spectra were recorded using a 10 cm gas cell with KBr windows. Elemental analyses were performed by Desert Analytics (Tucson, Ariz.). Gas chromatography mass spectrometry (GCMS) data were obtained using a JEOL JMS-GC Mate II spectrometer. Powdered lithium (Aldrich), lithium tetrahydroaluminate (Aldrich), trichloro(p-tolyl)silane (Gelest), trifluoromethane sulfonic acid (Alfa Aesar), nonafluorobutane-1-sulfonic acid (Aldrich) and electronic grade germane gas (Voltaix, Inc.) were used as received. The starting materials p-tolylsilane, chloro(p-tolyl)silane, 1,2-bis(p-tolyl)disilane and 1,2-bis(trifluoromethylsulfonyloxy)disilane were prepared according to literature procedures and their purity checked by NMR spectroscopy. Potassium germyl was synthesized in monoglyme using sodium-potassium (80% K) alloy. The coupling reactions using powdered lithium were performed in a helium environment rather that in an N₂ atmosphere to prevent formation of lithium nitride.

(p-tolyl)₂(SiH₂)₂.

A solution of monochloro(p-tolyl)silane (10.0 g, 63.8 mmol) in di-n-butyl ether (120 mL) and toluene (40 mL) is stirred with sodium pieces (1.68 g, 146.2 mmol) for 5 h at 125° C. The mixture is filtered and the filtrate is distilled to remove the solvents and other impurities. The remaining colorless liquid product (4.40 g, ˜60%) was examined by NMR to determine its identity and purity and was subsequently used without purification.

(C₄F₉SO₃)₂(SiH₂)₂:

A sample of C₄F₉SO₃H (7.9 g, 26.3 mmol) was added to a 15 mL solution of 1,2-(p-tolyl)disilane (3.18 g, 13.1 mmol) in toluene at −40° C. A colorless precipitate was immediately formed at low temperatures. The reaction flask was warmed to 23° C. and stirred for 1-2 h. The colorless solid was filtered and dried in vacuo. Repeated concentration and cooling of the toluene filtrate at −20° C. yielded additional product. Yield=7.9 g (95%). Mp=68° C. ¹H NMR (300 MHz, CDCl₃): δ5.078 (s, ¹J_(SiH)=272 Hz, Si—H₂, ³J_(HH)=3.6 Hz). ²⁹Si NMR (79.5 MHz, CDCl₃): δ—30.1. Anal. Calcd for C₈F₁₈S₂O₆Si₂H₄: C, 14.59; H, 0.61; F, 51.95. Found: C, 14.27; H, 0.87; F, 51.74.

(H₃Ge)₂(SiH₂)₂, method A:

A 20 mL solution of (C₄F₉SO₃)₂(SiH₂)₂ (4.67 g, 9.5 mmol) was added to a slurry of KGeH₃ (2.00 g, 20.9 mmol) in diethyl ether (15 mL), at −40° C. The reaction was then warmed to −10° C. and stirred under nitrogen for 12 h after which it was heated at 35° C. for an additional 1 h. The volatiles were fractionally distilled several times through U-traps held at −20, −50 and −196° C. The −50° C. trap retained pure (H₃Ge)₂(SiH₂)₂ (260 mg, 26% Yield) while the −196° C. trap contained solvent, and traces GeH₄ and SiH₄. Vapor pressure: 7.0 Ton (23° C.). IR (gas, cm⁻¹): 2147 (s), 2073 (vs), 910 (w), 879 (w), 799 (s), 740 (vw), 682 (s), 651 (m), 442 (vw). ¹H NMR (400 MHz, C₆D₆, 7.15 ppm): δ 3.106 (t, J=4.1 Hz, 6H, Ge—H₃), 83.290 (q, J=3.9 Hz, 4H, Si—H₂). ²⁹Si NMR (79.5 MHz, C₆D₆): δ—105.0 (this value is close to that observed for (H₃Ge)₂SiH₂ at −102.45) GCMS: m/z 210-196 (Si₂Ge₂H_(x) ⁺), 180-170 (SiGe₂H_(8-x) ⁺), 152-143 (Ge₂H_(6-x) ⁺), 140-126 (Si₂GeH_(8-x) ⁺), 107-98 (H₃SiGeH₃ ⁺), 77-72 (GeH₄), 62-58 (Si₂H_(6-x) ⁺), 32-28 (SiH₄ ⁺).

(H₃Ge)₂(SiH₂)₂, method B:

A sample of (CF₃SO₃)₂(SiH₂)₂ (3.39 g, 9.5 mmol) was added to a slurry of 2.40 g (20.9 mmol) of KGeH₃ in diethyl ether (30 mL) at −30° C. The mixture was then warmed to 23° C. and stirred under nitrogen for 5 h. The volatiles were fractionally distilled and the (H₃Ge)₂(SiH₂)₂ product in its pure form was collected at a −50° C. trap (0.250 g, ˜13% yield).

(SiH₂GeH₂)(GeH₃)₂:

The compound is obtained as a byproduct in the synthesis of (H₃Ge)₂(SiH₂)₂, and was isolated by repeated distillation through U-traps under static vacuum maintained at −20 and −50° C. to collect SiH₂GeH₂(GeH₃)₂ and (H₃Ge)₂(SiH₂)₂, respectively. Vapor pressure: 1.0 Torr (22° C.). IR (gas, cm⁻¹): 2145 (m), 2073 (vs), 910 (w), 878 (w), 793 (vs), 723 (w), 679 (w), 615 (s), 443 (vw). ¹H NMR (400 MHz, C₆D₆, 7.15 ppm): δ 3.30 (sept, J=3.9 Hz, 2H, Si—H₂), δ 3.23 (t, J=4.6 Hz, 3H, Ge—H₃), δ 3.13 (t, J=3.90 Hz, 3H, Ge—H₃), δ 3.03 (sept, J=4.0 Hz, 2H, Ge—H₂). ²⁹Si NMR (79.5 MHz, C₆D₆): δ—98.2. GCMS: m/z 256-240 (SiGe₃H_(10-x) ⁺), 230-212 (SiGe₂H_(8-x) ⁺)_(,) 184-169 (SiGe₂H_(8-x) ⁺), 154-141 (Ge₂H_(6-x) ⁺), 136-128 (Si₂GeH_(8-x) ⁺), 108-98 (SiGeH_(6-x) ⁺), 77-70 (GeH_(4-x) ⁺), 32-28 (SiH₄ ⁺).

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We claim:
 1. A semiconductor structure, comprising a substrate; and an Si—Ge layer comprising an Si—Ge backbone that consists essentially of the reaction products of one or more compounds selected from the group consisting of GeH₃—SiH₂—GeH₂—GeH₃; GeH₃—GeH₂—GeH₂—GeH₂—SiH₃; GeH₃—GeH₂—GeH₂—SiH₂—GeH₃; GeH₃—GeH₂—SiH₂—GeH₂—GeH₃; GeH[(SiH₃)(GeH₃)(GeH₂)](GeH₃); GeH[(GeH₃)₂(GeH₂)](SiH₃); SiH[(GeH₃)₂(GeH₂)](GeH₃); and GeH[(GeH₃)₂ (SiH₂)](GeH₃).
 2. The semiconductor structure of claim 1 wherein the Si—Ge layer comprises an SiGe film having a thickness of less than one micron.
 3. The semiconductor structure of claim 1 wherein the Si—Ge layer comprises an SiGe film having a density of threading defects of 10⁶/cm² or less.
 4. The semiconductor structure of claim 1 wherein the Si—Ge layer comprises an SiGe film having a substantially atomically planar surface morphology.
 5. The semiconductor structure of claim 1, wherein the one or more compounds include at least two compounds selected from the group.
 6. The semiconductor structure of claim 1, wherein the Si—Ge layer comprises an Si—Ge backbone that consists essentially of the reaction products of one or more compounds selected from the group consisting of GeH₃—GeH₂—GeH₂—GeH₂—SiH₃; GeH₃—GeH₂—GeH₂—SiH₂—GeH₃; GeH₃—GeH₂—SiH₂—GeH₂—GeH₃; GeH[(SiH₃)(GeH₃)(GeH₂)](GeH₃); GeH[(GeH₃)₂(GeH₂)](SiH₃); SiH[(GeH₃)₂(GeH₂)](GeH₃); and GeH[(GeH₃)₂ (SiH₂)](GeH₃).
 7. The semiconductor structure of claim 6 wherein the Si—Ge layer comprises an SiGe film having a thickness of less than one micron.
 8. The semiconductor structure of claim 6 wherein the Si—Ge layer comprises an SiGe film having a density of threading defects of 10⁶/cm² or less.
 9. The semiconductor structure of claim 6 wherein the Si—Ge layer comprises an SiGe film having a substantially atomically planar surface morphology.
 10. The semiconductor structure of claim 6, wherein the one or more compounds include at least two compounds selected from the group. 